US6251317B1

US6251317B1 - Method for manufacturing a ceramic composite material

Info

Publication number: US6251317B1
Application number: US09/284,221
Authority: US
Inventors: Robert Lundberg; Magnus Holmquist; Anthony G. Razzell; Ludovic Molliex; Olivier Sudre; Michel Parlier; Fabrice Rossignol; Julien Parmentier
Original assignee: Office National dEtudes et de Recherches Aerospatiales ONERA; Societe Nationale dEtude et de Construction de Moteurs dAviation SNECMA; Rolls Royce PLC; Volvo Aero AB
Current assignee: Office National dEtudes et de Recherches Aerospatiales ONERA; Safran Aircraft Engines SAS; Rolls Royce PLC; GKN Aerospace Sweden AB
Priority date: 1997-08-11
Filing date: 1997-08-11
Publication date: 2001-06-26
Anticipated expiration: 2017-08-11
Also published as: ES2164364T3; WO1999007653A1; JP2001502290A; EP0946458B1; EP0946458A1; DE69708682D1; DE69708682T2; CA2268019A1; CA2268019C

Abstract

The present method of manufacturing a ceramic composite material, composed of matrix and reinforcing materials and an intermediate weak interfice material, creates a composite material particuarly intended for use at temperatures above 1400° C. and in an oxidizing environment. The matrix and reinforcing materials consist of the same or different ceramic oxides having a melting point above 1600° C. The interface material provides in combination with the matrix and reinforcing materials a stress field liable to micro aciding. The reinforcing material is immersed into a powder slurry containing carbon (C) and ZrO₂so as to be coated thereby and then dried. After which, the thus created composite material is subjected to green forming and densifying steps. Finally, the composite material undergoes a heat-treatment in air leaving a porous structure of the interface material.

Description

This application claims the benefit of PCT Application Serial No. PCT/SE97/01340, filed Aug. 11, 1997.

BACKGROUND OF THE INVENTION

1. Field of the Invention

The present invention refers to a method of manufacturing a ceramic composite material comprising matrix and reinforcing materials and an intermediate weak interface material, said composite material being particularly intended for use at temperatures above 1400° C. and in an oxidizing environment, the matrix and reinforcing materials consisting of the same or different ceramic oxides having a melting point above 1600° C., and the interface material providing in combination with said materials a stress field liable to micro-cracking.

2. Description of the Related Art

For obtaining an intentional cracking behaviour of such ceramic composites various suggestions have been made, for instance according to WO 93/22258 to the Applicant. In practice, however, it has turned out that an interface layer of ZrO₂provides a bonding which mostly is too strong. On the other hand, carbon provides a suitably weak bonding between the reinforcing material and the matrix but degrades the fiber material. Over ZrO₂also HfO₂fulfills the requirements as to a weak interface zone but in many connections a still weaker interface is desirable.

SUMMARY OF THE INVENTION

Therefore, the main object of the present invention is to suggest a method by which an even weaker interface is obtained. In one aspect of the invention, the reinforcing fiber material is immersed into a powder slurry containing carbon and ZrO₂so as to be coated thereby and then dried, after which the composite material is subjected to green forming and densification steps as known per se, and finally a heat-treatment in air leaving a porous structure of the interface material. In another aspect of the invention, the reinforcing fiber material is immersed into and coated with a first powder slurry contain WO ing ZrO₂and then dried and immersed into and coated with a second powder slurry containing carbon and dried, after which the composite material is subjected to green forming and densification steps as known per se, and finally a heat-treatment in air leaving a gap between the reinforcing material and the matrix. It is advantageous to use a powder slurry technique, in which thus rather great particles are used which create a stable porous layer when a coating is used including C/ZrO₂.

By the present invention it is thus possible to obtain a weak interface securing the necessary crack deflection and fiber pullout behaviour during fracture of the composite.

The coating formed on fibers of which the reinforcing material consist and which are immersed in the slurry has proved to be adherent and strong enough to survive green forming and densification processes. After densification the C is removed by heat treatment in air, leaving a gap or porosity in the oxide interface. The volume fraction of C can be varied to achieve the desired interface strength. The interface made by this invention is stable at high temperatures for long times because the pores have got the right size, i.a. are large enough.

According to the further aspect of the invention, there is provided, however, another way to obtain an interface weak enough, namely to add a fugitive layer. In this method, the reinforcement is first immersed in a C powder slurry, dried and then immersed in an oxide (ZrO₂) powder slurry, forming a double or sequential coating. Again, this coating is strong and adherent enough to survive green forming and densification. After densification the C is removed by heat treatment leaving a gap between the reinforcing material and the oxide interface. Surface roughness of the reinforcing and matrix materials is sufficient to give load transfer between reinforcing material and matrix material. The absence of bonding between the oxide interface and the reinforcing material will ensure effective crack deflection. The degree of load transfer and frictional sliding resistance between reinforcing material and matrix controlling the fiber pullout behaviour can be varied by varying the thickness of the fugitive C layer.

The presence of an oxide interface will prevent a possible carbothermal reduction of the surface of the reinforcing fiber material of single crystal Al₂O₃fibers (to Al₄C₃) which would degrade the mechanical properties by defects-created. The presence of oxide interface (especially in the case of a C/ZrO₂mixture) will locally raise the partial pressure of oxygen and thus prevent the carbothermal reduction to take place.

DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS EXAMPLE 1

Single crystal fibers of Al₂O₃(from Saphikon Inc., USA) were covered with a thin layer of C/ZrO₂mixture. This was made by immersing the fibers in a slurry of C/ZrO₂-powder in water. The volume proportions of C to ZrO₂was {fraction (1/1)}. After drying the coated fibers were stacked to a fiber preform in a plaster mould. A Al₂O₃powder slurry was poured thereon and a pressure gradient was applied to give good infiltration of the fiber preform.

After drying the green bodies were sintered by hot-pressing at 1400° C., 10 MPa for 70 minutes. The C was burnt out by heat treatment at 1250° C. for 10 hours leaving a porous ZrO₂layer. After sintering and heat treatment the porous ZrO2 was about 3 μm thick. The porous ZrO₂layer provided crack deflection and fiber pullout which was proved by bending tests. Furthermore, the porous ZrO₂layer was stable at 1400° C. for 1000 hours and still provided crack deflection and fiber pullout after this heat treatment which was proved by bending tests.

EXAMPLE 2

Example 1 was repeated however using HfO₂instead of ZrO₂.

EXAMPLE 3

Single crystal fibers of Al₂O₃(from Saphikon Inc., USA) were covered with at thin double layer of C and ZrO₂. This was made by first immersing the fibers in a slurry of ZrO₂-powder in water and then immersing the fibers in a slurry of C-powder in water. After drying the coated fibers were stacked to a fiber preform in a plaster mold. An Al₂O₃powder slurry was poured thereon and a pressure gradient was applied to give good infiltration of the fiber preform.

After drying the green bodies were sintered by hot-pressing at 1400° C., at 10 MPa for 70 minutes. The C was burnt out by heat treatment at 1250° C. for 10 hours leaving a gap of about 1 μm between the zirconia layer and the Al₂O₃matrix. After sintering and heat treatment the ZrO₂layer was about 3 μm of thickness and not bonded to the matrix. The gap between fiber and ZrO₂layer provided crack deflection and fiber pullout which was proved by bending tests. (Furthermore, the ZrO₂layer was stable at 1400° C. for 1000 hours and still provided crack deflection and fiber pullout after this heat treatment which was proved by bending tests.)

EXAMPLE 4

Example 3 was repeated however using HfO₂instead of ZrO₂.

EXAMPLE 5

Example 3 was repeated, however with the steps in slightly reversed order, i.e. by first immersing the fibers in a slurry of C-powder in water and then in a slurry of ZrO₂powder, with similar advantageous result.

Claims

What is claimed is:

1. A method for manufacturing a ceramic composite material comprising matrix and reinforcing materials and an intermediate weak interface material, said composite material being particularly intended for use at temperatures above 1400° C. and in an oxidizing environment, the matrix and reinforcing materials consisting of the same or different ceramic oxides having a melting point above 1600° C., and the interface material providing in combination with said matrix and reinforcing materials a stress field liable to micro-cracking, comprising:

immersing the reinforcing material in a powder slurry containing carbon (C) and ZrO₂so as to be coated thereby, thereby creating said composite material;

drying said composite material;

green forming and densifying said composite material; and

heat-treating said composite material in air leaving a porous structure of the interface material.

2. A method for manufacturing a ceramic composite material comprising matrix and reinforcing materials and an intermediate weak interface material, said composite material being particularly intended for use at temperatures above 1400° C. and in an oxidizing environment, the matrix and reinforcing materials consisting of the same or different ceramic oxides having a melting point above 1600° C. and the interface material providing in combination with said matrix and reinforcing materials a stress field liable to micro-cracking, comprising:

immersing the reinforcing material in and coating the reinforcing material with a first powder slurry containing ZrO₂immersing the reinforcing material in and coating the reinforcing material with a second powder slurry containing carbon, thereby creating said composite material;

drying the reinforcing material;

green forming and densifying said composite material; and

heat-treating said composite material in air leaving a gap between the reinforcing material and the matrix.

3. A method according to claim 2, further comprising immersing the reinforcing material, after said immersing the reinforcing material in and coating the reinforcing material with a second powder slurry, into the first slurry so as to be provided with an outermost ZrO₂coating.